Silica molded bodies having low thermal conductivity

ABSTRACT

Hydrophobic shaped silica bodies having low density and low thermal conductivity are produced by forming a dispersion of silica in a solution of binder and organic solvent, and removing the solvent and shaping to form a shaped body. The shaped bodies retain their hydrophobicity, are stable with regards to shape, and are useful in acoustic and thermal insulation.

CROSS REFERENCE TO RELATED APPLICATIONS

This application is the U.S. National Phase of PCT Appln. No.PCT/EP2016/078739 filed Nov. 24, 2016, which claims priority to PCTApplication No. PCT/EP2015/077854 filed Nov. 26, 2015, the disclosuresof which are incorporated in their entirety by reference herein.

BACKGROUND OF THE INVENTION 1. Field of the Invention

The invention relates to high-viscosity crosslinkable silicone rubbercompositions, the inventive properties of which enable the production ofelastomeric shaped bodies by means of ballistic additive methods (3Dprinting).

2. Description of the Related Art

Numerous methods are available for the production of elastomericmoldings proceeding from crosslinkable silicone rubber compositions.According to the consistency and mechanism of cross linking of thesilicone rubber composition, moldings can be produced, for example, byinjection molding, by compression molding, by extrusion methods, bycalendering, casting, etc. What is common to these conventional methodsis that the properties of the molding formed (hardness, tear resistance,extensibility, color etc.) are fixed essentially by the physicalcomposition of the cross-linkable silicone rubber composition, whichmeans that these methods typically afford silicone moldings that aresubstantially isotropic in terms of their mechanical, optical andelectrical properties. The shape of the silicone parts formed in thisway is fixed either through use of specific molds (injection molds,press-molding molds, casting molds), within which the crosslinking iseffected, or by means of extrusion dies, calendering rolls etc.

However, the conventional processing methods are increasingly meetingtheir limits when silicone moldings of more complex geometry, ofdifferent material composition and/or of variable profiles of propertiesare required. The general trend toward individualization and individualadjustment of everyday articles is additionally requiring smallernumbers of items (e.g. prototypes, individually adapted prostheses,etc.), the necessity of rapid availability, and simple changeover to newproduct series, which means that, conventional methods are no longerefficient.

A method that is becoming increasingly important for production ofmoldings is the additive manufacturing method (3D printing method),which comprises numerous different techniques having the common factorof automated additive layer buildup of the molding (A. Gebhardt,Generative Fertigungsverfahren [Additive Manufacturing Methods], CarlHanser Verlag, Munich 2013). The additive manufacturing method not onlymakes it possible to avoid the above mentioned shortcomings of theconventional processing methods, but also enables a fundamentally newdesign of molded articles.

The additive layer-by-layer buildup of the molding can be effected bycrosslinking an applied layer of the cross-linkable material in alocation-selective manner, for example by means of a laser.Location-selective crosslinking means that only that material in thelayer which forms the later molded, article is crosslinked; theuncrosslinked material is ultimately removed and can optionally bereused. However, additive layer-by-layer buildup of the molding can alsobe effected by applying the crosslinkable material in alocation-selective manner (for example by means of a printhead in theform of discrete droplets), i.e. only at those sites that will be partof the shaped body to be formed. The layer applied in this way willgenerally not be continuous, but will directly reflect a cross sectionof the desired shaped body. The material applied in a location-selectivemanner is subsequently crosslinked (for example by full-areairradiation), and the next layer is applied in a location-selectivemanner, etc. If necessitated by the shape of the part to be printed (forexample in the case of overhanging structures, cavities etc.), it ispossible to apply a suitable support material in addition to thecrosslinkable silicone material, which can be removed again after theprinting operation has ended. The location-selective application of thecrosslinkable material can be effected, for example, by means ofdiscontinuous (discrete) jetting of droplets (so called “ballisticmethods”) or by continuous dispensing of thin strands. In principle,jetting as compared with dispensing enables the printing of finerstructural details and more complex structures. The advantage ofdispensing is that it is possible to apply greater amounts of materialper unit time. In addition, dispensing enables application ofhigher-viscosity materials as well, such that it can be advantageous tocombine the two techniques by also mounting one or, if appropriate, morethan one dispensing nozzle in addition to the jetting nozzle(s) in the3D printer. In this way, it is possible, for example, to form filigreeparts of the shaped body by means of the jetting nozzle and to printlarger voluminous parts of the shaped body by dispensing. With regard tothe rheological demands that jetting and dispensing make on the materialto be printed, jetting is found to be significantly more demanding.

WO2015/10733 A1 describes a 3D printing method for production ofprostheses from silicone elastomers by (continuous) extrusion of thecrosslinkable silicone rubber composition from a mixing nozzle. The 3Dprinting is optionally assisted by a second mixing nozzle for extrusionof a thermoplastic material which serves as support material for thesilicone rubber composition to be printed. The crosslinking of thesilicone rubber composition is effected by platinum-catalyzed additionreaction at room temperature (hydrosilylation). A disadvantage of thisprocess is the unachievable spatially exact positioning of ultrasmallamounts of silicone rubber composition for the printing of fine details.Furthermore, it is no longer possible to influence the juncture ofcrosslinking after the mixing of the two rubber components, onedisadvantage of which is that, in the course of the printing operation,regions of the silicone rubber composition having very different degreesof orosslinking are brought into contact (when the processing time forthe rubber composition is shorter than the printing time), or that theprinted structure is not self-supporting (processing time longer thanprinting time).

A specific embodiment of the additive manufacturing method is that ofthe ballistic method which features location-selective application ofthe crosslinkable composition with the aid of a printhead in the form ofindividual droplets (voxels) (jetting; inkjet printing; drop-on-demandprinting). The composition applied can subsequently be crosslinked, forexample by means of electromagnetic radiation, and thus forms a thinlayer of the molding. This operation of layer-by-layer buildup isrepeated until the complete shaped body has been formed.

In the case of the ballistic methods (jetting), a basic distinction isdrawn between continuous Inkjet (CIJ) printing and drop-on-demand (DOD)Inkjet printing. Both methods can generate droplets having diameters of10 μm up to a few hundred μm.

In the CIJ method, a continuous stream of droplets is generated byexpulsion of the material from a nozzle under high pressure andbreakdown of the resultant liquid jet to individual droplets as a resultof Rayleigh instability. The electrostatically charged droplets aredirected by means of electrical deflecting plates such that they eitherarrive at a precise location on the working plane (substrate) or (ifthere is to be no printing) arrive in a return channel through whichthey can be sent to reuse. This recycling of the material to be printed,in the case of crosslinkable silicone rubber compositions, as well asthe contamination risk, has the serious danger of bulk alteration of therheological properties owing to incipient crosslinking and is thereforeimpractical.

By contrast, in the DOD method, droplets are only produced if required,all of which are deposited in a location-selective manner for formationof the molding, either in that a positioning robot exactly positions thejetting nozzle in the x, y, z direction or in that the working plane ismoved correspondingly in the x,y,z direction; in principle, both optionscan also be implemented simultaneously.

DE 10 2011 012 412 A1 and DE 10 2011 012 480 A1 describe an apparatusand a method for stepwise production of 3-D structures with a printheadarrangement having at least two, preferably 50 to 200, printheadnozzles, which enables the location-selective application of optionallymultiple photo-crosslinkable materials with different photosensitivity,wherein the pnotocrosslinkable materials can subsequently beconsolidated in a location-selective manner by electromagneticradiation, especially by two-photon or multiphoton processes in thefocus region of a laser. The application of the photo-crosslinkablematerials by means of inkjet printing places specific demands on theviscosity of the pnotocrosslinkable materials. For instance, thepnotocrosslinkable materials feature a viscosity of less than 200 mPa·s,especially less than 80 mPa·s, more preferably less than 40 mPa·s.However, typical silicone rubber compositions, especially high-viscositysilicone rubber compositions, nave a viscosity several orders ofmagnitude higher and therefore cannot be jetted with the Inkjet printnozzles described here. In order to achieve adequate crosslinking of thematerial applied by means of two- or multiphoton polymerization,photoinitiators matched to the laser wavelength and a polymericcrosslinker component containing photocrosslinkable groups areadditionally required, where the photocrosslinkable groups belong to theclass of the acrylates, methacrylates, acrylamides, methacrylamides,urethane acrylates, urethane methacrylates, urea acrylates and ureamethacrylates. However, the method described is unsuitable forproduction of moldings consisting of silicone elastomers. Firstly, thephotoinitiators, photosensitizers, coinitiators etc. that are used haveonly sparing solubility in the (nonpolar) silicone compositions, whichleads to cloudiness, microphase separation and inhomogeneity. As iswell-known, the free-radical curing of silicones functionalized with theaforementioned pbotocrosslinkable groups has the problem of inhibitioncaused by oxygen, which considerably lowers the crosslinking rate andresults in tacky surfaces. If this effect is counteracted by increasingthe function density of acrylate groups, for example, the result isnonelastic, brittle vulcanizates. Finally, the extremely high localphoton density which is required for multiphoton polymerization(especially as a result of the low function density ofphotopolymerizable groups) and is generated by means of pulsedfemtosecond lasers causes breakdown reactions (carbonization) in thesilicone, which leads to unacceptable discoloration and damage to thematerial.

In the DOD method, the resolution of structural details of the shapedbody to be formed depends in particular on the size of the dropletsjetted (voxels) and the spatially exact application thereof. In general,it is possible to generate finer structural details by means of smallerdroplets. Since the frequency with which the printhead produces thedroplets is limited, the use of smaller droplets will, however,inevitably lead to longer production times for the molding, and so acompromise has to be made in the individual case between dimensionalaccuracy and production time. However, the size of the droplets, whichcan be varied within wide limits through suitable design of theprinthead, depends to a crucial degree on the rheological properties ofthe crosslinkable composition. It is generally the case thatlow-viscosity compositions permit the jetting of smaller droplets withhigher frequency, whereas higher-viscosity compositions cause thecurrently available printheads to rapidly reach their limits.

A more detailed consideration of the jetting method shows that asatisfactory print (i.e. a dimensionally exact elastomer part) isobtained only when the technical parameters of the printhead arecompatible with the properties, especially the rheological properties,of the material to be printed. Essential technical parameters of theprinthead are the pressure differential between the material reservoirand nozzle outlet, the nozzle diameter and the time within which theentire amount of a droplet leaves the nozzle (ejection time). Usefulprintheads especially include (thermal) bubblejet and piezo printheads,particular preference being given to piezo printheads, which are alsoable to jet higher-viscosity materials, for the printing of elastomerparts. These are commercially available (e.g. printheads from “NORDSONCORP./USA” and “VERMES MICRODISPENSING GMBH/Germany”). These piezoprintheads enable a pressure buildup in the kbar range, which means thatamounts of liquid in the pl to nl range can be expelled within 1-100 μsthrough a nozzle having diameters between 50 and 500 μm with a speed of1-100 m/s. This operation is repeated with a frequency of up to a fewhundred Hz (these are typical size ranges, which can differ considerablyin the individual case). In addition to these technical parameters ofthe print valves, the rheological properties of the material to beprinted are also found to be crucial. It is important to emphasize thatthe material does not leave the nozzle as finished droplets; instead, adroplet formation process proceeds. The material leaves the nozzle atfirst in the form of a laminar jet, with rapid formation of ovalthickening (because of the main droplet) at the head end, but this stillremains bound to the nozzle outlet via a thinner material thread.Subsequently, various scenarios are possible. If the material threadbecomes detached at the nozzle outlet and subsequently combines with themain droplet, the result is a single drop, the speed of which slowsconsiderably owing to the elastic combining process. If, by contrast,the material thread becomes detached both at the nozzle outlet and atthe main droplet, elastic contraction can result in formation of asecond droplet (satellite). The satellite and main droplet can hit thesubstrate surface one after another (working plane), but can also stillcombine during the flight phase to give a single droplet. However, thematerial thread that has become detached can also narrow at multiplepoints and ultimately form multiple satellite droplets, all of which cansubsequently hit the substrate.

If the material thread does not become detached immediately at thenozzle outlet, the portion of the material thread remaining at thenozzle outlet will contract, resulting in blockage of the nozzle, whichleads to failure of the printhead. Considering, moreover, that themovement robot that positions the printhead in the x,y planecontinuously traverses the x,y plane (i.e. without stopping at theindividual points (x,y)), it becomes understandable that the formationof satellites will inevitably lead to a fuzzy print, since the printnozzle, by the time at which the material thread becomes detached at thenozzle outlet, has already moved further in the direction of the next(x,y) point (typical speeds of the movement unit are between 0.1 and 1m/s).

The droplet that hits the working plane at high speed can likewisebehave in different ways. It can be deformed, for example, to give asphere segment-like, sphere-like or donut-like shape, where the usuallycircular footprint of this shape has a greater diameter than the nozzleas a result of the outward spread of the droplet. The droplet can alsoform a crown-like shape on impact, which then immediately splashes tinydroplets in the radial direction. This splashing also leads to anunclean print. The positioned droplets, owing to the extremely highshear rate in the nozzle, as a result of slow relaxation to the startingviscosity, can still have a very low viscosity and spread outward toosignificantly. For this reason, thixotropic additives, which bring abouta rapid recovery in viscosity of the jetted compound and prevent anexcessive outward spread or splashing, are added to silicone rubbercompositions having relatively low viscosity, which shall be understoodto mean viscosities of less than 300 Pa·s (at 25° C. and 0.5 s⁻¹). Onthe other hand, excessively rapid relaxation to the high startingviscosity in the presence of a yield point can lead to droplet shapeslike a conical hat, having a rough surface for lack of adequateleveling. Shear-thickening rheological characteristics of the dropletcan even lead to rebound of the impacted droplet.

It will be apparent to the person skilled in the art from the above thatonly through the exact matching of the technical parameters of theprinthead with the rheological material properties is the production ofhigh-quality molded articles possible. In the case of production ofmoldings proceeding from silicone rubber compounds by means of ballistic3D printing methods, there are some additionally complicating boundaryconditions. The production of silicone elastomers having good mechanicalproperties (elongation at break, extensibility, tear propagationresistance etc.) is only possible when a) sufficiently long siliconepolymers (i.e. with a sufficiently high degree of polymerization ormolecular weight) are used and b) actively reinforcing fillers (fumedsilicas, carbon blacks etc.) are simultaneously present in thecomposition. Both of these lead unavoidably to silicone rubber compoundshaving high viscosity, which is a barrier to clean droplet formation injetting. High viscosities, which shall be understood to mean viscositiesof 300 Pa·s to 10 kPa·s (at 25° C. and 0.5 s⁻¹), make the rapiddetachment of the material thread at the nozzle outlet more difficult,meaning that the main droplet remains connected to the nozzle via thematerial thread for a comparatively long period, while the printheadpermanently moves onward. Secondly, for the rapid formation of adiscrete droplet in jetting, a high surface tension of the material isnecessary. Surface tension always causes minimization of the surfacearea of a shape, meaning that it aims for a sphere shape, which canprevent satellite formation and splashing, for example. However, thesurface tension of silicones is among the lowest in the field ofelastomers (even lower surface tensions are possessed only byperfluorinated hydrocarbons). Because of these disadvantages in terms ofviscosity and surface energy, the production of elastomeric shapedbodies from high-viscosity silicone rubber compounds by the jettingmethod was considered to be non-implementable to date. Indeed, thispoint of view is also supported by numerous scientific publications. Ifthe materials to be jetted and print valves are characterized byproperties crucial to processibility, namely nozzle diameter, expulsionspeed, droplet speed, droplet volume, density, surface tension andviscosity at process shear rate, it is possible to define characteristicdimensionless parameters that describe the interplay of the inertiaforces, viscous forces, surface tensions, flow properties, frictionforces etc. that occur in jetting. These parameters include, forexample, the Reynolds number, the Ohnesorge number, the Weber number andthe Z number. Using these numbers, it is possible to infer parameterranges within which jetting (without satellite formation, splashing,blocking etc.) should be possible (cf., for example, Brian Derby, InkjetPrinting of Functional and Structural Materials: Fluid PropertyRequirements, Feature Stability, and Resolution, Annu. Rev. Mater. Res.2010. 40:395-414). If the typical properties of silicone rubbercompounds are entered into these equations, irrespective of the choiceof technical parameters of the printhead, this does not lead to the“green” parameter range, which suggests that jetting of high-viscositysilicone rubber compounds which meets the demands of 3D printing shouldnot be possible.

Even though some manufacturers of print valves state processibleviscosities of up to about 2 million mPa·s (at low shear rate), it isfound in practice that materials of such high viscosity generally cannotbe jetted because the pressure needed to expel the material droplet isinadequate owing to the high material viscosity and the print valvebecomes blocked.

SUMMARY OF THE INVENTION

It is an object of the present invention to provide silicone rubbercompositions that meet the demands on processing properties and time foruse in ballistic additive methods (3D printing), and hence enablehigh-quality industrial production of elastomeric shaped bodies. Inextensive tests, it has been found that, unexpectedly, only thehigh-viscosity silicone rubber compositions of the invention aresuitable for production of high-quality elastomeric moldings by means of3D printing in a ballistic method since these compositions, by virtue ofthe formulation, have specific rheological properties. It was found thatthe degree of shear-thinning characteristics, characterized by a nominalmelt flow index n, has to have the magnitude for n according to theinvention. More particularly, it has been found that, surprisingly, itis the nature of the shear-thinning characteristics characterized bymeans of the melt flow index n in the case of high-viscosity siliconerubber compounds that is crucial to the quality of the printed image andnot, for instance, as would seem likely, the much lower viscosity (η₂)which is established after strong shear on the silicone rubber compoundowing to the shear-thinning characteristics. It is thus found that,surprisingly, neither the starting viscosity (η₁) nor the finalviscosity (η₂) which is established after strong shear is crucial; whatis instead crucial is the nature and extent of the shear-thinningcharacteristics, characterized by the nominal melt flow index n.

BRIEF DESCRIPTION OF THE DRAWINGS

FIG. 1 illustrates a 3D article printed from an inventive printingcomposition.

FIG. 2 illustrates a further 3D article printed from an inventiveprinting composition.

FIG. 3 illustrates a 3D article printed from a non-inventive printingcomposition.

FIG. 4 illustrates a further 3D article printed from a non-inventiveprinting composition.

DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENTS

The advantage of the high-viscosity silicone rubber compositions of theinvention is that, without exception, they afford a high-quality printedimage, whereas noninventive high-viscosity silicone rubber compositionslead either to blocking and sticking of the print valve or to acrust-like appearance.

The high-viscosity silicone rubber compositions of the invention for the3D printing of silicone moldings by the ballistic additive DOD methodhave a viscosity n₁ (in each case at 25° C. and 0.5 s⁻¹) in the rangefrom 300 Pa·s to 10 kPa·s, and comprise

(A) 50% to 95% by weight of at least one organosilicon compound havingan average of at least two aliphatically unsaturated groups permolecule,

(B) 1% to 10% by weight of at least one organosilicon compound having anaverage of at least two SiH groups per molecule,

or, in place of (A)+(B) or in addition to (A) and (B), (G) 0%-95% byweight of at least one organosilicon compound having an average of atleast two aliphatically unsaturated groups and at least two SiH groupsper molecule,

(C) 0.1 to 500 ppm by weight of at least one hydrosilylation catalyst,based on the content of the metal relative to the overall siliconecomposition,

(D) 1% to 50% by weight of at least one actively reinforcing material,

(E) 0% to 30% by weight of auxiliaries other than (D),

characterized in that the nominal melt flow index n of the siliconerubber composition is within the following range:

−1.00<n<−0.40,

where n is calculated from formula (X):

log η=log K+n*log v  (X)

where

η represents the viscosity at shear rate v,

K represents the nominal consistency index,

v represents the shear rate and

log represents the decadic logarithm,

and the viscosity η₁, the nominal melt flow index n and the nominalconsistency index K in formula (X) are determined by the rheologicaltest method disclosed in the description.

The nature and the extent of the shear-thinning characteristics andhence the degree of the shear-thinning characteristics are characterizedby the nominal melt flow index n, where n<0 describes shear-thinningflow characteristics, n>0 describes shear-thickening flowcharacteristics and n=0 describes newtonian flow characteristics.

The high-viscosity silicone rubber compositions of the inventionpreferably have a viscosity η₁ (in each case at 25° C. and 0.5 s⁻¹) inthe range from 400 Pa·s to 5 kPa·s, and more preferably from 500 Pa·s to3 kPa·s,

The nominal melt flow index n of the silicone rubber compositions of theinvention is preferably in the range of −0.80<n<−0.45 and morepreferably in the range of −0.70<n<−0.50.

Constituent (A) of the silicone rubber compositions of the invention isan organosilicon compound having at least two aliphatic carbon-carbonmultiple bonds, preferably linear or branched polyorganosiloxanescomposed of units of the formula (I):

R_(a)R¹ _(b)SiO_((4-a-b)/2)  (I)

where

R may be the same or different and is a C₁-C₂₀ radical which is free ofaliphatic carbon-carbon multiple bonds, is optionallyhalogen-substituted and optionally contains oxygen, nitrogen, sulfur orphosphorus atoms,

R¹ may be the same or different and is a monovalent, optionallysubstituted organic radical having an aliphatic carbon-carbon multiplebond,

a is 0, 1, 2 or 3 and

b is 0, 1 or 2,

with the proviso that a+b<4 and there is an average of at least 2 R¹radicals per molecule.

The R radical may comprise mono- or polyvalent radicals, in which casethe polyvalent radicals, such as bivalent, trivalent and tetravalentradicals, connect a plurality of, for example two, three or four, siloxyunits of the formula (I) to one another.

Preferably, the R radicals are bonded to the silicon via a carbon oroxygen atom. Examples of SiC-bonded R radicals are alkyl radicals (e.g.methyl, ethyl, octyl and octadecyl radicals), cycloalkyl radicals (e.g.cyclopentyl, cyclohexyl and methylcyclohexyl radicals), aryl radicals(e.g. phenyl and naphthyl radicals), alkaryl radicals (e.g. tolyl andxylyl radicals) and aralkyl radicals (e.g. benzyl and beta-phenylethylradicals). Examples of substituted R radicals are3,3,3-trifluoro-n-propyl, p-chloropbenyl, chloromethyl, glycidozypropyland —(CH₂)_(n)—(OCH₂CH₂)_(m)—OCH₃, where n and m are identical ordifferent integers from 0 to 10. Examples of SiO-bonded R radicals arealkoxy groups (e.g. methoxy, ethoxy, iso-propoxy and tert-butoxyradicals) and the p-nitrophenoxy radical.

The R¹ radical may be any desired groups amenable to an additionreaction (hydrosilylation) with an SiH-functional compound. The R¹radical preferably comprises alkenyl and alkynyl groups having 2 to 16carbon atoms, such as vinyl, ally, methallyl, 1-propenyl, 5-nexenyl,ethynyl, butadienyl, hexadienyl, undecenyl, cyclopentenyl,cyclopentadienyl, norbornenyl and styryl radical, particular preferencebeing given to vinyl, allyl and hexenyl radicals.

If the R¹ radical comprises substituted aliphatically unsaturatedgroups, preferred substituents are halogen atoms, cyano groups andalkoxy groups. Examples of substituted R¹ radicals are allyloxypropyland isopropenyloxy radicals.

Preference is given, as constituent (A), to the use of vinyl-functional,essentially linear polydiorganosiloxanes having a viscosity of 100 to500,000 mPa·s, more preferably between 1000and 50,000 mPa·s (at 25° C.and 0.8 sec⁻¹). Constituent (A) may be a mixture of differentorganosilicon compounds of the type described above.

The content of constituent (A) in the silicone rubber composition of theinvention is 50% to 95% by weight, preferably 70% to 90% by weight, morepreferably 65% to 80% by weight.

Constituent (B) is any SiH-functional organosilicon compound having anaverage of at least two SiH groups. Constituent (B) functions ascross-linker of the silicone rubber composition. Constituent (B) mayalso be a mixture of various SiH-functional organosilicon compounds.Preferably, constituent (B) is linear, cyclic, branched or resinouspolyorganosiloxanes having Si-bonded hydrogen atoms, composed of unitsof the formula (II)

R_(c)H_(d)SiO_((4-c-d))/2  (II)

where

R may be the same or different and has the definition given above,

c is 0, 1, 2 or 3 and

d is 0, 1 or 2,

with the proviso that the sum total of (c+d) is not more than 3and thereis an average of at least two Si-bonded hydrogen atoms per molecule.

Preferably, constituent (B) contains Si-bonded hydrogen in the rangefrom 0.04 to 1.7 percent by weight (% by weight) based on the totalweight of the organopolysiloxane (B). The molecular weight ofconstituent (B) may vary within wide limits, for instance between 10²and 10⁶ g/mol. For example, constituent (B) may be an SiH-functionaloligosiloxane of relatively low molecular weight, such astetramethyldisiloxane, but may also be high-polymericpolydimethylsiloxane having SiH groups in chain or terminal positions ora silicone resin having SiH groups. Preference is given to the use ofSiH-functional compounds of low molecular weight, such astetrakis(dimethyl-siloxy)silane and tetramethylcyclotetrasiloxane, andSiH-containing siloxanes, such as poly(hydrogenmethyl)siloxane andpoly(dimethylhydrogenmethyl) siloxane having a viscosity of 10 to 1000mPa·s (at 25° C. and 0.8 sec⁻¹). Preference is given to constituents (B)that are compatible with constituent (A) (homogeneously miscible or atleast emulsifiable). According to the type of constituent (A), it maytherefore be necessary to suitably substitute constituent (B), forexample by replacing some of the methyl groups with3,3,3-trifluoropropyl or phenyl groups.

Constituent (B) may be used individually or in the form of a mixture ofat least two different (B) and is preferably present in the siliconerubber composition of the invention in such an amount that the molarratio of SiH groups to aliphatically unsaturated groups is 0.1 to 20,preferably between 0.5 and 5, more preferably between 1 and 2. Thecontent of constituent (B) in the silicone rubber composition of theinvention is 0.1 to 15% by weight, preferably 0.5%-10% by weight, morepreferably 2%-5% by weight.

Constituent (G) can be used in place of (A)+(B) or in addition to (A)and (B). In the addition-crosslinking compositions of the invention, thefollowing combinations are thus possible: (A)+(B) or (A)+(G) or (B)+(G)or (A)+(B)+(G) or (G) alone. (G) is an organosilicon compound having atleast two aliphatically unsaturated groups and at least two SiH groupsper molecule and can thus crosslink with itself. Compounds (G) are knownto those skilled in the art from the prior art. If compounds (G) areused, they are preferably those composed of units of the generalformulae

R⁷ _(k)SiO_((4-k)/2)  (VI),

R⁷ _(m)R⁶SiO_(3-m)/2)  (VII)

and

R⁷ _(o)HSiO_(3-o/2)  (VIII),

where

R⁷ is a monovalent, optionally substituted hydrocarbyl radical which isfree of aliphatic carbon-carbon multiple bonds and has 1 to 18 carbonatoms per radical and

R⁶ is a monovalent hydrocarbyl radical having a terminal aliphaticcarbon-carbon multiple bond having 2 to 8 carbon atoms per radical,

k is 0, 1, 2 or 3,

m is 0, 1 or 2,

o is 0, 1 or 2,

with the proviso that, in (G), there is an average of at least 2 R⁶radicals and an average of at least 2 Si-bonded hydrogen atoms.

It is possible to use a single compound (G) or a mixture of at least twocompounds (G).

The content of constituent (G) in the silicone rubber composition of theinvention is 0%-95% by weight, preferably 0%-50% by weight, morepreferably 0%-10% by weight.

Constituent (C) serves as catalyst for the addition reaction(hydrosilylation) between the aliphatically unsaturated groups ofconstituent (A) and the silicon-bonded hydrogen atoms of constituent (B)or (G). In principle, it is possible to use any hydrosilylationcatalysts typically used in addition-crosslinking silicone rubbercompositions. As catalysts (C) that promote addition of Si-bondedhydrogen onto aliphatic multiple bonds, for example, platinum, rhodium,ruthenium, palladium, osmium or iridium, an organometallic compound or acombination thereof are suitable. Examples of such catalysts (C) aremetallic and finely divided platinum which may be present on supports,such as silicon dioxide, aluminum oxide or activated carbon, compoundsor complexes of platinum, such as platinum halides, e.g. PtCl₄,H₂PtCl₆.6H₂O, Na₂PtCl₄.4H₂O, platinum acetylacetonate and complexes ofthese compounds, encapsulated in a matrix or a core/shell-likestructure, platinum-olefin complexes, platinum-phosphite complexes,platinum-alcohol complexes, platinum-alkoxide complexes, platinum-ethercomplexes, platinum-aldehyde complexes, platinum-ketone complexes,including reaction products of H₂PtCl₆.6H₂O and cyclohexanone,platinum-vinyisiloxane complexes, such asplatinum-1,3-divinyl-1,1,3,3-tetramethyldisiloxane complexes with orwithout a content of detectable inorganically bound halogen,bis(gamma-picoline)-platinum dichloride, trimethylenedipyridineplatinumplatinum dichloride, trimethylenedipyridineplatinum dichloride,dicylopentadieneplatinum dichloride, dimethylsulfoxide-ethyleneplatinum(II) dichloride, and reaction products of platinum tetrachloride witholefin and primary amine or secondary amine or primary and secondaryamine, such as the reaction product of platinum tetrachloride dissolvedin 1-octene with sec-butylamine or ammonium-platinum complexes,trimethylcyclopentadienylplatinum(IV), trimethyl[(3-trimethoxysilyl)propylcyclopentadienyl]platinum(IV).

The hydrosilylation catalysts listed generally enable rapid crosslinkingof the silicone rubber composition even at room temperature. Since thehydrosilylation reaction sets in immediately after mixing of allconstituents, addition-crosslinking compositions are usually formulatedin the form of at least two components, where a component A comprisesthe platinum catalyst (C) and another component B comprises thecrosslinker (B) or (G). In order to have a sufficient processing timeeven after mixing of the two components, inhibitors which delay theonset of the orosslinking reaction are usually added. Rapid crosslinkingcan then be brought about by supply of neat. For the use ofaddition-crosslinking compositions in the 3D printing method, however,preference is given to those hydrosilylation catalysts which can barelybe activated by thermal means but can be very readily activated byhigh-energy radiation (UV, UV-VIS), meaning that the deposited siliconerubber composition of the invention is crosslinked not with thermalinitiation but preferably with initiation by UV or UV-VIS radiation.This is effected, for example, either via an activatable hydrosilylationcatalyst or via a deactivatable inhibitor (F) which is additionallypresent. Compared to thermal crosslinking, UV- or UV-VIS-inducedcrosslinking has numerous advantages. Firstly, the intensity, period ofaction and locus of action of the UV radiation can be judged accurately,whereas the heating of the silicone rubber composition depositeddropwise (and the subsequent cooling thereof) is always retarded byvirtue of the relatively low thermal conductivity. Because of theintrinsically very high coefficient of thermal expansion of thesilicones, the temperature gradients that are inevitably present in thecourse of thermal crosslinking lead to mechanical stresses which have anadverse effect on the dimensional accuracy of the molding formed, whichin the extreme case can lead to unacceptable distortions of shape. Afurther advantage of the UV/VIS-induced addition crosslinking is foundin the production of multicomponent moldings, for example hard-softcomposites which, as well as the silicone elastomer, comprise athermoplastic, the thermal warpage of which is avoided.

UV/VIS-induced addition-crosslinking silicone rubber compositions aredescribed, for example in DE 10 2008 000 156 A1, DE 10 2008 043 316 A1,DE 10 2009 002 231 A1, DE 10 2009 027 486 A1, DE 10 2010 043 149 A1 andWO 2009/027133 A2. The crosslinking takes place through UV/VIS-inducedactivation of a light-sensitive hydrosilylation catalyst (C), preferencebeing given to platinum catalysts activatable by UV or UV-VIS radiation.The technical literature describes numerous light-activatable platinumcatalysts which are largely inactive with exclusion of light and can beconverted to platinum, catalysts that are active at room temperature byirradiation with light having a wavelength of 250-500 nm. Examples ofthese are (η-diolefin) (σ-aryl) platinum complexes (EP 0 122 008 A1; EP0 561 919 B1), Pt (II)-β-diketonate complexes (EP 0 398 701 B1) and(η⁵-cyclopentadienyl)tri(σ-alkyl)platinum(IV) complexes (EP 0 146 307B1, EP 0 358 452 B1, EP 0 561 893 B1). Particular preference is given toMeCpPtMe₃ and the complexes that derive therefrom through substitutionof the groups present on the platinum, as described, for example, in EP1 050 538 B1 and EP 1 803 728 B1.

The silicone rubber compositions which crosslink in a UV- orUV-VIS-induced manner can be formulated in single- or multicomponentform.

The rate of UV/VIS-induced addition crosslinking depends on numerousfactors, especially on the nature and concentration of the platinumcatalyst, on the intensity, wavelength and action time of the UV/VISradiation, the transparency, reflectivity, layer thickness andcomposition of the silicone rubber composition, and the temperature. Forthe activation of the UV/VIS-induced addition-crosslinking siliconerubber compositions, light of wavelength 240-500 nm, preferably 300-450nm, more preferably 350-400 nm, is used. In order to achieve rapidcrosslinking, which is understood to mean a crosslinking time at roomtemperature of less than 20 min, preferably less than 10 min/morepreferably less than 1 min, it is advisable to use a UV/VIS radiationsource with a power between 10 mW/cm² and 15,000 mW/cm⁸, and a radiationdose between 150 mJ/cm² and 20,000 mJ/cm², preferably between 500 mJ/cm²and 10,000 mJ/cm². Within the scope of these power and dose values, itis possible to achieve area-specific irradiation times between a maximumof 2000 s/cm² and a minimum of 8 ms/cm². It is also possible to use twoor more radiation sources, including different radiation sources.

The hydrosilylation catalyst should preferably be used in acatalytically sufficient amount, such that sufficiently rapidcrosslinking is enabled at room temperature. Typically, 0.1 to 500 ppmby weight of the catalyst is used, based on the content of the metalrelative to the overall silicone rubber composition, preferably 0.5-200ppm by weight, more preferably 1-50 ppm by weight. It is also possibleto use mixtures of different hydrosilyation catalysts.

Constituent (D)

The term “actively reinforcing material” or, synonymously, “reinforcingmaterial” is understood in the context of this invention to mean an(actively) reinforcing filler. Compared to (inactive) non-reinforcingfillers, actively reinforcing fillers improve the mechanical propertiesof the elastomers in which they are used. Inactive fillers, by contrast,act as extenders and dilute the elastomer. The terms “activelyreinforcing material”, “actively reinforcing filler”, “reinforcingmaterial” and “reinforcing filler” are used synonymously in the contextof the present invention.

Constituent (D) is necessary in order to achieve adequate mechanicalstrength of the silicone elastomer. Mechanical strength is understood tomean the entirety of the properties typical of elastomers, especiallyhardness, elongation at break, tear resistance and tear propagationresistance. In order to achieve appealing properties in this regard, theaddition of actively reinforcing materials is indispensable. Theseinclude, in particular,

(D1) finely divided particulate materials such as fumed silicas,titanium dioxides, aluminum, oxides, aerogels and carbon blacks having ahigh specific surface area between 50 and 1000 m²/g (measured by the BETmethod to DIN 66131 and DIN 66132), and

(D2) nanoparticies (SiO₂, TiO₂, exfoliated sheet silicates, carbonnanotubes etc.).

Preferably, component (D) is selected from the group consistingexclusively of (D1) fumed silicas, titanium dioxides, aluminum oxides,aerogels and carbon blacks having a high specific surface area between50 and 1000 m²/g, measured by the BET method to DIN 66131 and DIN 66132,and (D2) nanoparticies consisting of SiO₂, TiO₂, exfoliated, sheetsilicates or carbon nanotubes.

Preference is given to using (D1) as a reinforcing filler. Aparticularly active and preferred reinforcing agent (D1) is fumed silica(produced, for example, by reaction of silicon-halogen compounds in ahydrogen-oxygen flame).

Fumed silica is hydrophilic because of the silanol groups (—SiOH)present on the surface thereof. However, it is customary and preferableto use hydrophobic silicas in silicone rubber compositions in order toachieve higher filler contents (and hence better mechanical properties)without an excessive rise in viscosity and without phase inversion.Moreover, the mixing of the silicone constituents and the silica issignificantly facilitated by the hydrophobic character. Thehydrophobization of the silica, which is effected mainly by silylation,is known to those skilled in the art and is described, for example, inpublished specifications EP 686676 B1, EP 1433749 A1 and DE 102013226494A1. As a result of the hydrophobization (silylation) of the silicasurface, there is a reduction in the silanol group density typicallyfrom 1.8 to 2.5 SiOH/nm² down to less than 1.8 to less than 0.9 silanolgroups per nm² (determined by means of acid-base titration as stated inG. W. Sears, Anal. Chem. 1956, 28, 1981). At the same time, there is anincrease in the carbon content of the silica to 0.4% to 15% by weight ofcarbon (determined by means of elemental analysis), the weight beingbased on the hydrophobic silica.

The use of reinforcing agents (D2) is possible but not preferred,because it is impracticable on the industrial scale. Because of the veryminor intermolecular interactions between silicones, the production oftrue nanoparticulate silicone rubber compositions is found to be verydifficult. There is usually rapid re-agglomeration of the nanoparticles,or there is no exfoliation or intercalation of sheet silicates in thesilicone.

It is also possible to use a plurality of different reinforcing agents(D).

The content of reinforcing agents (D) based on the overall crosslinkablesilicone rubber composition is between 1% and 50% by weight, preferablybetween 5% and 30% by weight, more preferably between 10% and 25% byweight.

Constituent (E) is known to those skilled in the art and includes ailoptional additives that may be present in the silicone rubbercomposition of the invention in order to achieve specific profiles ofproperties. These include inhibitors, heat stabilizers, solvents,plasticizers, color pigments, sensitizers, photoinitiators, adhesionpromoters, inactive fillers, thixotropic agents, conductivity additives,silicone resins etc. that are different than the other constituents.

What is to be shown hereinafter is how the nominal melt flow index n andthe viscosity η₁, which are crucial for the processing of high-viscositysilicone compositions by the DOD-3D printing method, can be adjusted ina controlled manner.

The particulate materials (D1) and (D2) detailed above are among thereinforcing fillers. By contrast with the non-reinforcing fillers, forexample chalk, quartz flour, polymer powders etc., reinforcing fillershave a high specific surface area, which results in a very nigh numberof filler-filler and filler-silicone interactions. These interactionsbring about the desired high mechanical strength of the resultingsilicone elastomer.

A further means of achieving a high level of mechanical strength andelasticity is the use of long-chain (and hence higher-viscosity)silicone polymers. Silicone compositions containing short-chain siliconepolymers can be crosslinked to give very hard materials, but give lesstear-resistant and less elastic silicone elastomers.

The use of reinforcing fillers in combination with long-chain siliconepolymers, by virtue of the abovementioned interactions, leads torelatively high-viscosity silicone compositions. However, the viscosityof the silicone composition is often limited at the upper end (and oftenalso additionally at the lower end) by the desired processing method.For instance, the extremely high-viscosity (firm/pasty) solid siliconerubbers are typically processed by the press-molding method or bycalendering etc.

Processing by the DOD-3D printing method is increasingly meeting itslimits with silicone compositions of ever higher viscosity in spite ofall technological advances. In the individual case, it is thereforenecessary to make a compromise between the desired high mechanicalstrength of the silicone elastomer and the processibility of theuncrosslinked silicone composition.

In principle, one is confronted with the problem of keeping theviscosity of the silicone composition η₁ as low as possible for reasonsof processibility, but at the same time of achieving maximum mechanicalstrength values. The viscosity of the silicone composition η₁ (since itis measured at very low shear, which can also be regarded as viscosityat rest or starting viscosity) is fixed in particular by the nature andcontent of reinforcing filler (D) and the chain length (viscosity) ofthe silicone polymers used (components (A, (B) and/or (G)).

One skilled in the art knows of numerous ways of keeping the viscositylow without significantly reducing the mechanical strength values. Theseinclude, for example, the hydrophobization of the filler (for example bysilylation of finely divided silicas), which can reduce the increase inviscosity caused by the filler to an enormous degree. In addition, it ispossible to keep the viscosity of the silicone composition low throughthe use of relatively short-chain vinyl-terminated silicone polymers(component (A)) in combination with relatively short-chain SiH-terminalsilicone polymers (component (B)) or through the use of relativelyshort-chain silicone polymers of component (G); in this case, it is onlyin the course of the crosslinking reaction that the long-chain siliconepolymers are constructed through chain extension (i.e. only after theactual processing step such as the jetting).

If the viscosity η₁ is found to be too high, i.e. more than 10 kPa·s (at25° C. and 0.5 s¹), it is thus possible to counteract this by (i)lowering the filler concentration, (ii) increasing the hydrophobicity ofthe filler (for example by using hydrophobic fillers or byhydrophobizing hydrophilic fillers) and/or (iii) lowering the polymerchain length of the silicone constituents. The exact adjustment of theviscosity η₁ can thus be achieved by simple routine experiments.

However, the viscosity at rest η₁ is not the only crucial factor for theprocessibility of a silicone composition by the DOS method. Theviscosity at the extremely high shear rates that occur in the jettingnozzle is also of great significance. Processibility of high-viscositycompounds by the DOD method becomes possible at all only by virtue ofthe fact that the viscosity decreases enormously with increasing shearrate. These characteristics are referred to as shear-thinningcharacteristics. The decrease in the viscosity as a result of shear maybe several orders of magnitude in the DOB method. For the processibilityof high-viscosity silicone compositions by the DOD method, markedshear-thinning characteristics are thus indispensable.

The shear-thinning characteristics can be well-characterised by thenominal melt flow index n. The nominal melt flow index n describes thedeviation from what are called newtonian flow characteristics, whichfeature a shear rate-independent viscosity and are characterized by theflow index n=0. n values of greater than 0 describe an increase inviscosity with increasing shear rate (shear-thickening characteristics).n values of less than zero describe shear-thinning characteristics, i.e.a decrease in viscosity with increasing shear rate. This relationshipcan be described by equation (IX) (the logarithmic form of equation (IX)is identical to equation (X)):

η(v)=K*v ^(n)  (IX)

where η(v) denotes the viscosity η at the shear rate v and K is thenominal consistency index (when n=0, i.e. in the case of newtoniancharacteristics, K=η).

In order to determine the two parameters K and n present in the equation(IX), it is sufficient to know two pairs of values (η₁ at v₁) and (η₂ atv₂). For the first pair of values, it is possible, for example, to usethe viscosity at rest η₁ at v₁=0.5 s⁻¹. Since the shear rate range thatoccurs on jetting is difficult to attain for measurement purposes(requiring measurements in a high-pressure capillary viscometer), forexample, the viscosity η₂ at v₂=25 s⁻¹ is taken for the second pair ofvalues, but this does not constitute a restriction owing to theexperimentally confirmed validity of equation (IX).

Silicone compositions generally nave shear-thinning characteristics,meaning that the nominal melt flow index n is negative. However, it hasbeen found that, surprisingly, irrespective of the processibility of thesilicone compound, which may quite possibly be processible under highshear given a sufficiently low viscosity, a satisfactory printed imageis obtained by the DOD-3D printing method only when the nominal meltflow index n is within a particular range. It is thus quite possiblethat a compound having lower viscosity at high shear will give a poorerprinted image than a compound having higher viscosity at the same shear.In fact, a crucial factor is found to be the degree of theshear-thinning characteristics, i.e. the significance of the decrease inviscosity that occurs when the shear rate is increased. In other words:a sufficiently low viscosity at high shear rate is a necessary conditionfor processibility by the DOB method, but is not a sufficient conditionfor a good printed image. A necessary and simultaneously sufficientcondition for this is the abovementioned relation

−1<n<−0.40.

There are in principle the following options for bringing the nominalmelt flow index n into the range of the invention:

Silicone polymers feature virtually newtonian flow characteristics overa wide shear rate range; only at very high shear rates is there anyorientation of the polymer chains in the flow direction, which causes adecrease in viscosity. For this reason, it is less effective to adjustthe melt flow index n via an altered composition of the siliconeconstituents (components (A), (B) and/or (G)).

A much more effective method is found to be the adjustment of theshear-thinning characteristics through suitable choice of thereinforcing filler. More particularly, it is possible to adjust thesurface energy of the filler such that the filler particles form afiller network based on physical interactions in the hydrophobic,nonpolar silicone matrix. At rest, this filler network hinders theflowability of the silicone constituents, but breaks down as soon asthere is relatively strong shear on the silicone composition, meaningthat the flowability of the silicone constituents increasessignificantly under strong shear, which is equivalent to markedshear-thinning characteristics.

The breakdown of the filler network brought about by the strong shear isreversible, meaning that the compound returns to its originalequilibrium state after the shear has stopped (relaxation).

More exact analysis of these shear-thinning characteristics caused bythe filler shows that an increase in the surface energy of the filleraggregates is associated with stronger and quicker formation of thefiller network, which in turn results in a rise in the startingviscosity (viscosity at rest) η₁.

This enhanced structure formation can be brought about, inter alia, bystructure-forming additives which increase the surface energy of thefiller. The enhanced structure formation can alternatively be broughtabout through the use of less strongly hydrophobic or hydrophobizedfillers. In addition, structure formation can be intensified by anincrease in the filler content. Given the same filler content, anincrease in the specific surface area of the filler also leads toenhanced structure formation of the silicone composition.

If the nominal melt flow index n is thus found to be too high, i.e. morethan −0.40, it is possible to counteract this by (i) lowering thehydrophobicty of the filler, (ii) by increasing the fillerconcentration, (iii) by using auxiliaries which can increase the surfaceenergy of the filler (for example thixotropic agents) and/or (iv) byincreasing the specific surface area of the filler. The person skilledin the art will thus be able to select the most suitable method takingaccount of the other boundary conditions to be placed on the siliconecomposition. The exact adjustment of the nominal melt flow index n canthus be achieved as described by simple routine experiments.

Silicone rubber compositions of the invention can be produced in one-,two- or multicomponent form. In the simplest case, production iseffected in the form of a one-component silicone rubber composition ofthe invention by homogeneous mixing of all components.

The silicone rubber compositions of the invention are used forproduction of elastomeric shaped bodies by means of ballistic additiveDOD methods (3D printing).

The present invention therefore further provides a process for producingelastomeric shaped bodies, characterized in that the shaped bodies areformed from the silicone rubber compositions of the invention by meansof ballistic additive DOB methods (3D printing).

Rheological test method for determination of the nominal consistencyindex K, the viscosities η₁ and η₂, and the nominal melt flow index n ofthe silicone rubber composition

All measurements were conducted in an Anton Paar MCR 302rheometer withair bearings at 25° C., unless stated otherwise, according to DIN EN ISO3219. Measurement was effected with plate-plate geometry (diameter 25mm) with a gap width of 300 μm. Excess sample material was removed bymeans of a wooden spatula after the plates had formed the measurementgap (called trimming).

Before the start of the actual measurement profile, the sample wassubjected to a defined preliminary shear in order to eliminate therheological history composed of sample application and formation of themeasurement position. This preliminary shear (measurement phase 1)comprises a shear phase of 60 s at a shear rate of v₁=0.5 s⁻¹, wherein aviscosity value is established very rapidly and remains constant. Thisviscosity value which is established at the end of measurement phase 1is referred to as η₁. Immediately thereafter, there is strong shear at ashear rate of v₁=25 s⁻¹that lasts for 60 s (measurement phase 2), whichresults in an abrupt drop in the viscosity, as a result of theshear-thinning characteristics, to a considerably lower value thatremains constant.

The viscosity value which is established in this case at the end ofmeasurement phase 2 is referred to as η₂. By inserting these two pairsof values (v₁; η₁) and (v₂; η₂) into formula (X), the two unknowns K(consistency index) and n (melt flow index) are calculated (twoequations with two unknowns):

log η=log K+n*log v  (X)

Determination of Viscosity

The viscosities were measured in an Anton Paar MCR 302rheometeraccording to DIN EN ISO 3219:1994 and DIN 53019, using a cone-platesystem (CP50-2 cone) with an opening angle of 2°. The instrument wascalibrated with 10000 standard oil from the National Metrology Instituteof Germany. The management temperature is 25.00° C.+/−0.05° C., themeasurement time 3 min. The viscosity reported is the arithmetic mean ofthree independently conducted individual measurements. The measurementuncertainty for the dynamic viscosity is 1.5%. The shear rate was chosendepending on the viscosity and is stated separately for each viscosityreported.

Examples

The examples which follow serve to illustrate the invention withoutrestricting it.

Rheological Test Method

Testing in the examples was effected analogously to the manner describedabove.

Conditioning of the Silicone Rubber Compositions

All the silicone rubber compositions used for DOB 3D printing weredevolatilized prior to processing, by storing 100 g of the compositionin an open PE can in a desiccator under a vacuum of 10 mbar at room,temperature for 3 h. Subsequently, the composition was dispensed into a30 ml cartridge having a bayonet seal with exclusion of air and sealedwith an appropriate expulsion plunger (plastic piston).

The Luer lock cartridge was then screwed into the vertical cartridgeholder of the Vermes dosage valve in a liquid-tight manner with the Luerlock screw connection downward and 3-8 bar compressed air was applied tothe pressure plunger at the top end of the cartridge; the expulsionplunger present in the cartridge prevents the compressed air fromgetting into the previously evacuated silicone rubber composition.

All UV-sensitive silicone compositions were produced under yellow light(with exclusion of light below 700 nm), devolatilized analogously anddispensed into opaque 30 ml cartridges with a Luer lock bayonet seal.

In order to prevent the silicone compositions from absorbing air duringstorage, the cartridge containers were packed under vacuum with aluminumfoil-covered PE inliners using a vacuum welding system from Landig+LavaGmbH & Co. KG, ValentinstraBe 35-1, D-88348 Bad Saulgau.

Raw Materials and, Silicone Rubber Compositions Used

Vinyl-Functional Polyorganosiloxanes as Per Constituent (A):

A1: vinyldimethylsiloxy-terminal polydimethylsiloxane having a viscosityof 20,000 cSt., available from ABCR GmbH, Karlsruhe, Germany under the“Poly(dimethylsiloxane), vinyldimethylsiloxy terminated; viscosity 20000cSt.” product name, cat. no. AB128873, CAS [68083-19-2] (ABCR catalog).

A2: vinyldimethylsiloxy-terminal polydimethylsiloxane having a viscosityof 500 000 cSt.; GAS No, [68083-19-2],

A3: vinyldimethylsiloxyl-terminal trifluoropropylmethyldimethylsiloxanecopolymer having a viscosity of 14 Pa·s and atrifluoropropylmethylsiloxy content of 42 mol %, available from ABCRGmbH, Karlsruhe, Germany, under the FMV-4031 name.

A4: vinyldimethylsiloxy-terminal polydimethylsiloxane having a viscosityof 200 cSt., available from ABCR GmbH, Karlsruhe, Germany under theproduct name DMS-V22, CAS [68083-19-2] (ABCR catalog).

A5: vinyldimethylsiloxy-terminal polydimethylsiloxane having a viscosityof 1000 cSt., available from ABCR GmbH, Karlsruhe, Germany under theproduct name DMS-V31, CAS [68083-19-2] (ABCR catalog).

SiH-Functional Crosslinkers as Per Constituent (B):

B1: methylhydrosiloxane-dimethylsiloxane copolymer having a molecularweight of Mn=1900-2000 g/mol and a methylhydrogensiloxy content of 25-30mol %, available from Gelest, Inc. (65933 Frankfurt am Main, Germany)under the product name HMS-301.

B2: SiH-terminated polydimethylsiloxane, CAS: 70900-21-9, available fromABCR GmbH, 7 6187 Karlsruhe, Germany, under the DMS-H31 name, viscosity1000 cSt.

B3: SiH-terminated polydimethylsiloxane, CAS: 70900-21-9, available fromABCR GmbH, 76187 Karlsruhe, Germany, under the DMS-H21 name, viscosity100 cSt.

B4: trimethylsiloxy-terminalmethylhydrodimethyltrifluoropropylmethylsiloxane copolymer having aviscosity of 170 mPa·s, an Si-bonded H content of 0.59% by weight and atrifluoropropylmethylsiloxy content of 15 mol %.

Hydrosilylation Catalyst as Per Constituent (C):

C1: UV-activatable platinum catalyst;trimethyl-(methylcyclopentadienyl)platinum(IV), available fromSigma-Aldrich®, Taufkirchen, Germany.

Reinforcing Agent as Per Constituent (D):

D1: a hydrophobized fumed silica having a BET surface area of 300 m²/gand a carbon content of 4.3% by weight was produced analogously topatent specification DE 38 39 900 A1 by hydrophobization usinghexamethyldisilazane from a hydrophilic fumed silica, Wacker HDK® T-30(available from WACKER CHEMIE AG, Munich, Germany).

D2: a hydrophobized fumed silica having a BET surface area of 300 m²/gand a carbon content of 4.7% by weight and a vinyl content of 0.2% byweight was produced analogously to patent specification BE 38 3 9 900 A1by hydrophobization using a mixture of hexamethyidisilazane and1,3-divinyltetramethyldisilazane from a hydrophilic fumed silica, WackerHDK® T-30 (available from WACKER CHEMIE AG, Munich, Germany).

Optional Constituent (E)

E1: stabilizer (inhibitor) 1-ethynylcyclohexanol; 99%, CAS No. 78-27-3,≥99%, available from ABCR GmbH, 76187 Karlsruhe, Germany

E2: Plasticizer, trimethylsiloxy-terminated polydimethylsiloxane, CASNo. 9016-00-6, available from ABCR GmbH, 76187 Karlsruhe, Germany, underthe DMS-T43 name, viscosity 30,000 cSt.

E3: thixotropic agent: epoxidized linseed oil, CAS No. 67746-08-1,“Edenol B 316 Special”; from Emery Oleochemicals GmbH, Henkelstr. 67,40589 Düsseldorf.

Inventive and Noninventive Examples 1-15

The silicone rubber compositions specified in tables 1, 2 and 3wereproduced by, in a first step, intimately mixing constituent (A) andconstituent (D) as described hereinafter in the weight ratios specifiedin tables 1, 2 and 3. For this purpose, 60% by weight of the total massof constituent (A) in the form of 255 g was initially charged in adouble-Z kneader at a temperature of 25° C. and the kneader was heatedto 70° C. On attainment of 70° C., the total amount of constituent (D),i.e. the hydrophobic fumed silica described as reactant D1 or D2,corresponding to the weight ratios given in tables 1, 2 and 3, wasmetered in and kneaded in in portions with continuously kneading overthe course of 1 hour, and the material was homogenized. Subsequently,the resultant material of relatively high viscosity was kneaded anddevolatilized under an oil-pump vacuum (<100 hPa) at 150° C. over thecourse of 1 hour. After this baking phase, the vacuum was broken and thetemperature was adjusted to room temperature. Then the remaining 40% byweight of the total mass of constituent (A), i.e. 170 g, were mixed inand the material was homogenized at room temperature over the course ofone hour.

The further production of the silicone rubber compounds was effected(under yellow light or with exclusion of light) by intimate mixing ofthe mixture of (A) and (D) produced by the method as described abovewith the other constituents (B), (E) and (C) in Speedmixer® screw topmixing beakers from Hauschild & Co. KG, Waterkamp 1, 5907 5 Hamm. Forthis purpose, the components were successively weighed into theappropriate mixing beaker and mixed manually. Subsequently, the beakerthat had been closed with an appropriate screwtop was mixed and degassedat 1500 rpm under a vacuum of 100 mbar in a vacuum Speedmixer® BAG 400.2VAC-P from. Hauschild & Co. KG, Waterkamp 1, 59075 Hamm for at least 5minutes.

Prior to the vacuum mixing operation in the vacuum Speedmixer®, a smallhole was drilled into the screwtop in order to allow the air to escapefrom the mixing beaker.

Subsequently, the material was dispensed from the mixing beaker into anopaque 30 ml Luer lock cartridge in an air-free manner (with the aid ofa Hauschild dispensing system, consisting of an appropriate speed discand a lever press). Subsequently, the cartridge was sealed with anappropriate expulsion plunger (plastic piston).

The compositions of the inventive and noninventive silicone rubbercompositions are given in tables 1 to 3.

TABLE 1 (all figures in % by weight except for C1 in ppm by weight basedon Pt metal): Constituent Ex. 1*) Ex. 2 Ex. 3*) Ex. 4 Ex. 5*) Ex. 6 A152.2 52.2 66.6 66.6 44.7 44.7 A2 21.7 21.7 — — — — B1 0.9 0.9 1.0 1.01.9 1.9 B2 — — 7.7 7.7 — — B3 2.9 2.9 — — — — C1 25 25 25 25 25 25 D122.4 22.4 24.8 24.8 19.1 19.1 E1 0.0025 0.0025 0.0025 0.0025 0.00250.0025 E2 — — — — 34.2 34.2 E3 — 0.05 — 0.05 — 0.05 Starting viscosityη₁ (at 25° C.; v₁ = 0.5 s⁻¹) η₁ [Pa · s] 448 1060 510 877 351 428 Finalviscosity η₂ (at 25° C.; v₂ = 25 s⁻¹) η₂ [Pa · s] 110 129 152 151 167 67Nominal melt flow index n n [−] −0.36 −0.54 −0.31 −0.45 −0.19 −0.47Nominal consistency index K K [Pa · s^(n)] 349 729 412 643 308 304*)noninventive

It can be inferred from table 1 that the shear-thinning characteristicsare insufficient, in the non-inventive examples 1, 3 and 5, resulting ina nominal melt flow index of more than −0.4. Through use of thethixotropic agent E3, which increases the surface energy of the fillerD1, it is possible to remedy this problem and establish a flow indexwithin the range claimed (cf. inventive examples 2, 4 and 6).

TABLE 2 (all figures in % by weight except for C1 in ppm by weight basedon Pt metal): Constituent Ex. 7 Ex. 8 Ex. 9 Ex. 10 Ex. 11 A1 — — 65.562.4 64.9 A3 72.0 70.0 — — — B1 — — 3.5 4.6 4.1 B4 3.0 3.0 — — — C1 2525 25 25 25 D1 25 27 20 — — D2 — — 10 33 31 E1 0.0025 0.0025 0.00250.0025 0.0025 E3 — — — — — Starting viscosity η₁ (at 25° C.; v₁ = 0.5s⁻¹) η₁ [Pa · s] 3410 4095 1780 3930 2570 Final viscosity η₂ (at 25° C.;v₂ = 25 s⁻¹) η₂ [Pa · s] 265 307 230 372 254 Nominal melt flow index n n[—] −0.65 −0.66 −0.52 −0.60 −0.59 Nominal consistency index K K [Pa ·s^(n)] 2173 2592 1239 2589 1706 *) noninventive

TABLE 3 (all figures in % by weight except for C1 in ppm by weight basedon Pt metal): Constituent Ex. 12*) Ex. 13*) Ex. 14* Ex. 15*) A1 16.216.2 31.7 31.7 A2 48.6 48.6 48.6 48.6 A4 18.3 18.3 — — A5 4.9 4.9 — — E13.9 3.9 3.9 3.9 Cl 25 25 25 25 D1 8.1 8.1 15.8 15.8 E1 0.0025 0.00250.0025 0.0025 E3 — 0.05 — 0.05 Starting viscosity η₁ (at 25° C.; v₁ =0.5 s⁻¹) η₁ [Pa · s] 99 126 311 354 Final viscosity η₂ (at 25° C.; v₂ =25 s⁻¹) η₂ [Pa · s] 78 79 131 136 Nominal melt flow index n n [—] −0.06−0.12 −0.22 −0.24 Nominal consistency index K K [Pa · s^(n)] 95 117 267299 *)noninventive

It can be inferred from tables 2 and 3 that, in the noninventiveexamples 12 to 15, the shear-thinning characteristics are insufficient,resulting in a nominal melt flow index of more than −0.4. This problemcan be remedied by increasing the filler concentration, and a melt flowindex within the range claimed can be established (cf. inventiveexamples 7 to 11 in table 2). The increase in the filler concentrationsimultaneously leads to a rise in the viscosity η₁ into the rangeclaimed.

DOD-3D Printer:

The silicone rubber compositions produced were processed by the DODmethod in a “NEO-3D printer” manufacturing system from “German RepRapGmbH” to give silicone elastomer parts. For this purpose, theabovementioned 3D printer was modified and adapted. The thermoplasticfilament dosage unit that was originally installed in the “NEO-3Dprinter” was replaced by a jetting nozzle from “Vermes MicrodispensingGmbH, Otterfing”, in order to be able to deposit higher-viscosity tofirm pasty materials such as the silicone rubber compositions of theinvention in the DOD method.

Since the “NEO” printer was not equipped as standard for theinstallation of jetting nozzles, it was modified. The Vermes jettingnozzle was incorporated into the printer control system such that thestart-stop signal (trigger signal) of the Vermes jetting nozzle wasactuated by the G code controller of the printer. For this purpose, aspecial signal was recorded in the G code controller. The G codecontroller of the computer used this merely to switch the jetting nozzleon and off (starting and stopping of metering).

For the signal transmission of the start-stop signal, the heating cableof the originally installed filament heating nozzle of the “NEO” printerwas severed and connected via a relay to the Vermes nozzle.

The other dosage parameters (metering frequency, rising, failing etc.)of the Vermes jetting nozzle were adjusted by means of the MDC 3200+Microdispensing Control Unit.

The 3D printer was controlled by means of a computer. The softwarecontrol and control signal connection of the 3D printer (software:“Repetier-Host”) was modified to the effect that both the movement ofthe dosage nozzle in the three spatial directions and the signal fordroplet deposition were thus controllable. The maximum, speed, ofmovement of the “NEO” 3D printer was 0.3 m/s.

Dosage System:

The dosage system used for the silicone rubber compositions used was the“MDV 3200A” microdispensing dosage system from “Vermes MicrodispensingGmbH”, consisting of a complete system having the following components:a) MDV 3200 A—dosage unit with an attachment for Luer lock cartridges,with which 3-8 bar compressed air (hose with adapter) was applied to thetop end of the cartridge, b) Vermes MDH-230tfl left nozzle trace-heatingsystem, c) MDC 3200+ MicroDispensing Control Unit, which was in turnconnected to the PC controller and via movable cables to the nozzle,enabled the setting of the jetting dosage parameters (rising, falling,opentime, needlelift, delay, no pulse, heater, nozzle, distance, voxeldiameter, air supply pressure at the cartridge). Nozzles havingdiameters of 50, 100, 150 and 200 μm are available. It was thus possibleto precisely position ultrafine droplets of the silicone rubbercomposition in the nanoliter range at any desired xyz position on theworkbench or the already crosslinked silicone elastomer layer. Unlessstated otherwise, the standard nozzle set installed in the Vermes valvewas a 200 μm nozzle. The reservoir vessels used for the silicone rubbercomposition were upright 30 ml Luer lock cartridges that were screwedonto the dispensing nozzle in a liquid-tight manner and pressurized withcompressed air.

The modified “NEO” 3D printing and the “Vermes” dosage system werecontrolled with a PC and an open source software package “Simplify 3D”.

Jetting:

The silicone rubber compositions were repeatedly deposited dropwise inlayers of the desired geometry with the jetting nozzle parametersspecified hereinafter on a glass microscope slide of area 25×75 mm, withcontinuous irradiation and resultant crosslinking of the depositedmaterial over the entire printing operation (about 50 sec) with aBLUEPOINT irradiation system having an output of 13,200 mW/cm². Nozzlediameter: 200 μm, rising: 0.3 ms, failing: 0.1 ms, open time: 15 ms,needle lift: 100%, delay (surface pressure): 25 ms, delay (individualpoints for the voxel size measurement): 100 ms, heating: 45° C.,cartridge supply pressure: 3 bar.

In this way, it was possible to use the silicone rubber compositions ofthe invention to obtain transparent silicone elastomer molded parts ofdifferent geometry.

While the inventive high-viscosity silicone rubber compositions listedin tables 1-3, without exception, gave a high-quality printed image, thenoninventive high-viscosity silicone rubber compositions led either toblocking and sticking of the print valve or gave a crust-likeappearance. The inventive silicone rubber compositions have a melt flowindex n of less than −0.40 and could be jetted without any problem bythe DOD method (cf. inventive dot matrix in FIG. 1 and inventive spiralsilicone elastomer molding in FIG. 2). The appearance in the case of useof the noninventive compounds is shown by way of example by FIG. 3 forthe printed dot matrix and by FIG. 4 for the spiral silicone elastomermolding.

1.-7. (canceled)
 8. A process for producing shaped silica bodies havinga C content of less than 8% by weight, a density, determined by Hgporosimetry, of less than 0.30 g/cm³, a pore volume for pores smallerthan 4 μm, determined by Hg porosimetry, of more than 2.0 cm³/g, aproportion of the pores smaller than 4 μm, based on the total porevolume, of at least 60% and a thermal conductivity, determined by anon-steady-state method, of less than 30 mW/K*m, comprising: i)producing a dispersion containing silica, at least one binder and anorganic solvent, and ii) evaporating the solvent from the dispersion,and shaping to form the shaped silica bodies.
 9. The process of claim 8,wherein hydrophilic silica or a mixture of hydrophilic silica andpartially hydrophobic silica is as the silica.
 10. The process of claim8, wherein silanes containing a C₁-C₃-alkyl group, C₂₋₃ alkenyl group,methoxy group, ethoxy group, or a mixture thereof are used as a binder.11. The process of claim 8, wherein at least one solvent is selectedfrom the group consisting of alkanes, ethers, alcohols, and mixturesthereof.
 12. A shaped silica body produced by the process of claim 8.13. Acoustic or thermal insulation comprising shaped silica bodies ofclaim 12.